JPH059659A - Austenitic stainless steel having excellent corrosion resistance at high temperature - Google Patents
Austenitic stainless steel having excellent corrosion resistance at high temperatureInfo
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- JPH059659A JPH059659A JP16594691A JP16594691A JPH059659A JP H059659 A JPH059659 A JP H059659A JP 16594691 A JP16594691 A JP 16594691A JP 16594691 A JP16594691 A JP 16594691A JP H059659 A JPH059659 A JP H059659A
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- Prior art keywords
- high temperature
- creep rupture
- stainless steel
- austenitic stainless
- rupture strength
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は廃棄物燃焼環境等の溶融
塩化物および塩化水素（ＨＣｌ）ガス等に対して優れた
高温腐食特性を有するオーステナイト系ステンレス鋼に
関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an austenitic stainless steel having excellent high temperature corrosion characteristics against molten chloride such as waste combustion environment and hydrogen chloride (HCl) gas.
【０００２】[0002]
【従来の技術】現在、一般廃棄物および産業廃棄物の中
で、廃棄プラスチック類および自動車シュレッダーダス
ト等の燃焼により発生する高濃度の溶融塩化物およびＨ
Ｃｌガス等に対し、優れた高温腐食特性を有する焼却炉
および燃焼ボイラ用鉄鋼材料はない。そのために、現状
では、上記廃棄物は高い発熱量を持ちながら、不燃・燃
焼不適物として分別・収集され、主に埋め立てられてい
る。また、一部分別・収集されずに、一般廃棄物に混入
してボイラで燃焼される前記廃棄物は、腐食性環境条件
が厳しいためボイラの蒸気条件は圧力２９４．２Ｎ／ｃ
ｍ2 、温度３５０℃程度以下に抑えられ、効率の良い低
公害の燃料源として活用されていない。2. Description of the Related Art Currently, in general waste and industrial waste, high-concentration molten chloride and H generated by combustion of waste plastics and automobile shredder dust, etc.
There is no steel material for incinerators and combustion boilers that has excellent high-temperature corrosion properties for Cl gas and the like. For this reason, at present, the wastes have a high calorific value, but are sorted and collected as non-combustible / incombustible substances, and are mainly landfilled. Further, since the waste that is mixed into general waste and burned in the boiler without being separated and collected partly has severe corrosive environmental conditions, the steam condition of the boiler is pressure 294.2 N / c.
m 2, is suppressed to below a temperature of about 350 ° C., it is not used as a source of fuel efficient low emission.
【０００３】[0003]
【発明が解決しようとする課題】本発明は上記問題点を
解決するという観点にたって、廃棄物燃焼環境中の溶融
塩化物およびＨＣｌガス等に対して優れた耐高温腐食性
を有し、かつクリープ破断強度および製造時の熱間加工
性の良好なオーステナイト系ステンレス鋼を提供するこ
とを目的とする。In view of solving the above problems, the present invention has excellent high temperature corrosion resistance against molten chloride and HCl gas in a waste combustion environment, and An object is to provide an austenitic stainless steel having good creep rupture strength and hot workability during production.
【０００４】[0004]
【課題を解決するための手段】本発明の要旨とするとこ
ろは、重量％にて、Ｃ；０．０２〜０．１５％、Ｍｎ；
０．３〜２．０％、Ｃｒ；１８〜２５％、Ｎｉ；１７〜
５０％、Ｍｏ；０．５〜３．０％、Ｔｉ；０．０３〜
０．３％、Ｎｂ；０．０５〜０．６％、Ｂ；０．００３
〜０．０１％、Ｐ；０．０４％以下、Ｓ；０．００５％
以下、Ｎ；０．０２〜０．３％、Ｃａ；０．０００５〜
０．０５％を含有し、かつＡｌ；０．５〜６．０％、Ｓ
ｉ；０．７〜３．０％のうち１種以上を含み、残部がＦ
ｅおよび不可避的不純物からなるオーステナイト系ステ
ンレス鋼にあり、廃棄物燃焼環境での高温腐食特性とク
リープ破断強度および製造時の熱間加工性が良好なステ
ンレス鋼である。The gist of the present invention is that, in% by weight, C: 0.02 to 0.15%, Mn;
0.3-2.0%, Cr; 18-25%, Ni; 17-
50%, Mo; 0.5 to 3.0%, Ti; 0.03 to
0.3%, Nb; 0.05 to 0.6%, B; 0.003
~ 0.01%, P; 0.04% or less, S; 0.005%
Hereinafter, N: 0.02-0.3%, Ca: 0.0005-
0.05% and Al: 0.5-6.0%, S
i; contains at least one of 0.7 to 3.0% and the balance is F
It is an austenitic stainless steel consisting of e and unavoidable impurities, and has good high temperature corrosion characteristics in a waste combustion environment, creep rupture strength, and hot workability during manufacturing.
【０００５】[0005]
【作用】以下に成分の限定理由について説明する。先
ず、塩化物およびＨＣｌガスに対して高温腐食特性を向
上させる合金元素として、Ｎｉ、ＡｌおよびＳｉが有効
であることを見出した。Ｎｉ含有量増大により高温腐食
深さが減少する（図１）。これはスケール中に生成する
Ｎｉ富化層が塩化物およびＨＣｌガスに対する保護性を
有するためと考えられる。その効果は１７％未満では十
分ではないため下限を１７％とした。なお、Ｎｉ量が多
くなると熱間での加工硬化が起こりやすく熱間加工性が
劣化すること、またコストの面でもＮｉ量が多くなると
高価になるのでＮｉの上限を５０％とした。したがって
Ｎｉの量を１７〜５０％と限定した。The reason for limiting the components will be described below. First, it was found that Ni, Al and Si are effective as alloying elements for improving the high temperature corrosion characteristics with respect to chloride and HCl gas. The hot corrosion depth decreases with increasing Ni content (Fig. 1). It is considered that this is because the Ni-rich layer formed in the scale has protection against chloride and HCl gas. If the effect is less than 17%, the lower limit is set to 17%. It should be noted that the upper limit of Ni is set to 50% because if the Ni content increases, hot work hardening easily occurs and the hot workability deteriorates, and in terms of cost, if the Ni content increases, it becomes expensive. Therefore, the amount of Ni is limited to 17 to 50%.
【０００６】ＡｌおよびＳｉはその添加により高温腐食
深さが減少する（図２）。これはスケール中にそれぞれ
Ａｌ2 Ｏ3 およびＳｉＯ2 系の保護性スケールが生成す
るためと考えられる。その効果はＡｌ；０．５％未満、
Ｓｉ；０．７％未満では十分ではないため、Ａｌの下限
を０．５％、Ｓｉの下限を０．７％とした。なお、Ａｌ
およびＳｉ量が増加すると熱間加工性および高温クリー
プ破断強度が低下するので、両特性を確保するためにＡ
ｌ量を６．０％以下、Ｓｉ量を３．０％以下にすること
が必要である。これらの理由によってＡｌの量を０．５
〜６．０％、Ｓｉの量を０．７〜３．０％とした。The addition of Al and Si reduces the hot corrosion depth (FIG. 2). It is considered that this is because protective scales of Al 2 O 3 type and SiO 2 type are generated in the scale. The effect is Al; less than 0.5%,
Si; less than 0.7% is not sufficient, so the lower limit of Al was 0.5% and the lower limit of Si was 0.7%. In addition, Al
Since the hot workability and the high temperature creep rupture strength decrease as the amount of Si and Si increases, in order to secure both properties, A
It is necessary that the amount of 1 be 6.0% or less and the amount of Si be 3.0% or less. For these reasons, the amount of Al is 0.5
˜6.0% and the amount of Si was 0.7˜3.0%.
【０００７】Ａｌ、Ｓｉは単独添加または複合添加して
も同様の効果が得られるが、熱間加工性確保の観点か
ら、複合添加の場合の上限はＡｌ、Ｓｉの合計５．０％
が望ましい。次に、上記以外の成分について述べる。Ｃ
は、炭化物形成元素としてクリープ破断強度やクリープ
破断伸びに大きな影響を与えるので、Ｃ量はクリープ特
性に効果的なＣｒ、Ｍｏ、Ｔｉ、Ｎｂ、Ｂの炭化物を形
成するに必要な量を最小限添加する必要がある。一方、
溶接時高温割れを防止するためにはＣ量をできる限り下
げる必要がある。以上の観点からＣの下限を０．０２
％、上限を０．１５％と定めた。Similar effects can be obtained even if Al and Si are added alone or in combination, but from the viewpoint of ensuring hot workability, the upper limit in the case of compound addition is 5.0% in total of Al and Si.
Is desirable. Next, components other than the above will be described. C
Has a great effect on creep rupture strength and creep rupture elongation as a carbide-forming element, so the C content is the minimum necessary to form carbides of Cr, Mo, Ti, Nb, and B that are effective for creep properties. Need to be added. on the other hand,
In order to prevent hot cracking during welding, it is necessary to reduce the C content as much as possible. From the above viewpoint, the lower limit of C is 0.02.
%, And the upper limit was set to 0.15%.
【０００８】Ｍｎは、脱酸を十分行い健全な鋳片を得る
ために必要であり、鋼中に不純物として含有されるＳ成
分を固定し、熱間脆性を防止し、溶接性、熱間加工性を
向上させるので０．３％以上は必要である。しかし添加
量が多過ぎると耐酸化性を損なうので上限を２．０％と
した。Ｃｒは高温クリープ破断強度、硫酸塩等に対する
耐高温腐食性および耐高温酸化性等を向上させるので耐
熱合金にとっては必須の元素である。ＳＵＳ３４７Ｈ
（１８Ｃｒ−１２Ｎｉ−０．７Ｎｂ）と同等以上の耐高
温酸化性が必要なので、Ｃｒ量の下限をＳＵＳ３４７Ｈ
のＣｒ量と同量の１８％とした。しかしＣｒ量が多いと
長時間加熱によりσ脆化が起こりやすくなる。２５Ｃｒ
−２０Ｎｉのオーステナイト系ステンレス鋼ＳＵＳ３１
０Ｓ以上の耐σ脆化性を確保するためにＣｒ量の上限を
２５％とした。Mn is necessary for sufficient deoxidation to obtain a sound cast piece, and fixes the S component contained as an impurity in steel to prevent hot brittleness, weldability and hot working. 0.3% or more is necessary to improve the property. However, if the addition amount is too large, the oxidation resistance is impaired, so the upper limit was made 2.0%. Cr improves the high temperature creep rupture strength, the high temperature corrosion resistance to sulfates and the like, the high temperature oxidation resistance and the like, and is an essential element for the heat resistant alloy. SUS347H
Since high temperature oxidation resistance equal to or higher than (18Cr-12Ni-0.7Nb) is required, the lower limit of Cr content is SUS347H.
18%, which is the same as the Cr content of Cr. However, if the amount of Cr is large, σ embrittlement easily occurs due to long-term heating. 25Cr
-20Ni austenitic stainless steel SUS31
In order to secure σ embrittlement resistance of 0 S or more, the upper limit of Cr content was set to 25%.
【０００９】Ｍｏは固溶体硬化作用や析出硬化作用によ
ってクリープ破断強度を高めるのに必要な元素であるの
で下限を０．５％とした。しかしＭｏはσ相の形成を促
進し、長時間使用脆化を起こしやすいので添加量の上限
を３．０％とした。Ｔｉ、Ｎｂは炭・窒化物形成元素で
クリープ破断強度の向上に効果があり、複合添加でその
炭・窒化物が微細分散化する場合に最もクリープ破断強
度が高くなる。炭・窒化物の析出量はＴｉ量が０．０３
％未満、Ｎｂ量が０．０５％未満では十分でなく、一
方、Ｔｉ量が０．３％、Ｎｂ量が０．６％を超えてのＴ
ｉ、Ｎｂ複合添加では炭・窒化物が凝集粗大化し、クリ
ープ破断強度が低下する。以上の点を考慮してＴｉの量
を０．０３〜０．３％、Ｎｂの量を０．０５〜０．６％
とした。Since Mo is an element necessary for increasing the creep rupture strength by the solid solution hardening action and the precipitation hardening action, the lower limit was made 0.5%. However, since Mo promotes the formation of the σ phase and easily causes embrittlement during long-term use, the upper limit of the amount added is set to 3.0%. Ti and Nb are charcoal / nitride forming elements and are effective in improving the creep rupture strength, and the creep rupture strength becomes highest when the carbon / nitride is finely dispersed by complex addition. The amount of precipitation of carbon / nitride is 0.03 of Ti
%, Nb content less than 0.05% is not sufficient, while Ti content exceeding 0.3% and Nb content exceeding 0.6% results in T
When i and Nb are added together, carbon / nitride agglomerates and coarsens, and the creep rupture strength decreases. Considering the above points, the amount of Ti is 0.03 to 0.3% and the amount of Nb is 0.05 to 0.6%.
And
【００１０】Ｂはクリープ破断強度を高めるのに０．０
０３％以上は必要であるが添加量が多いと溶接性および
延性が劣化するので添加量の上限を０．０１０％とし
た。Ｐは添加量が多いと高温クリープ中に析出を促進
し、クリープ中脆化を促進させるので上限を０．０４％
とした。Ｓも粒界に偏析し高温クリープ中に粒界の脆化
を促進させるので上限を０．００５％とした。B is 0.0 to increase the creep rupture strength.
It is necessary to add 03% or more, but if the addition amount is large, the weldability and ductility deteriorate. Therefore, the upper limit of the addition amount is set to 0.010%. When P is added in a large amount, it promotes precipitation during high temperature creep and embrittlement during creep, so the upper limit is 0.04%.
And S also segregates at the grain boundaries and promotes embrittlement of the grain boundaries during high temperature creep, so the upper limit was made 0.005%.
【００１１】Ｎは高Ｃｒ、高Ｎｉ系オーステナイト合金
の高温クリープ破断強度を高めることが知られている。
Ｎは窒化物の形成によりクリープ破断強度を高めるが、
そのためには０．０２％以上にする必要がある。しかし
Ｎ量が増加するとクリープ破断伸びが減少し、またＮ量
が０．３％を超えても長時間のクリープ破断強度の増加
は少ない。したがってＮ量の上限を０．３％とした。N is known to increase the high temperature creep rupture strength of high Cr, high Ni austenitic alloys.
N increases creep rupture strength by forming a nitride,
For that purpose, it is necessary to make it 0.02% or more. However, when the N content increases, the creep rupture elongation decreases, and even when the N content exceeds 0.3%, the increase in the creep rupture strength for a long time is small. Therefore, the upper limit of the amount of N is set to 0.3%.
【００１２】Ｃａは脱酸・脱硫作用を有し、ＯおよびＳ
の粒界偏析を減少させることによって熱間加工性および
クリープ破断強度を向上させる。その効果は０．０００
５％未満では十分でないので、Ｃａ量の下限を０．００
０５％とした。また、Ｃａ量が０．０５％を超えると鋼
の清浄性を劣化し、熱間加工性を低下する。したがって
Ｃａ量の上限を０．０５％とした。Ca has a deoxidizing / desulfurizing action, and O and S
The hot workability and creep rupture strength are improved by reducing the grain boundary segregation of. The effect is 0.000
Since less than 5% is not sufficient, the lower limit of Ca content should be 0.00
It was set to 05%. Further, if the amount of Ca exceeds 0.05%, the cleanliness of steel deteriorates and the hot workability deteriorates. Therefore, the upper limit of the amount of Ca is set to 0.05%.
【００１３】[0013]
【実施例】次に本発明の実施例についてさらに具体的に
述べる。表１、表２（表１のつづき）に本発明例の化学
組成、高温腐食深さ、クリープ破断強度および熱間加工
性を、また、表３、表４（表３のつづき）に比較例の化
学組成、高温腐食深さ、クリープ破断強度および熱間加
工性を示す。EXAMPLES Next, examples of the present invention will be described more specifically. Tables 1 and 2 (continued from Table 1) show the chemical composition, high temperature corrosion depth, creep rupture strength and hot workability of the examples of the present invention, and Tables 3 and 4 (continued from Table 3) show comparative examples. Shows the chemical composition, high temperature corrosion depth, creep rupture strength and hot workability.
【００１４】いずれも４５ｋｇ真空溶製し、熱間押出、
固溶化熱処理の後、高温腐食試験およびクリープ破断試
験を行った。高温腐食試験は３７％ＮａＣｌ＋６３％Ｆ
ｅＣｌ2 合成灰を板状試験片表面に塗布し、０．２％Ｈ
Ｃｌ＋０．５％ＳＯ2 ＋５％Ｏ2 ＋１５％ＣＯ2 ＋ｂａ
ｌ．Ｎ2 ガス中で５５０℃×３０ｈ加熱し、試験片縦断
面の腐食深さを測定した。クリープ破断試験はゲージ部
φ６×l ３０ｍｍの試験片で温度５５０℃、応用４４
１．３Ｎ／ｍｍ2 の条件で行い、その破断時間でクリー
プ破断強度を評価した。また熱間加工性を熱間押出時の
割れ有無で評価した。In each case, 45 kg was vacuum melted, hot extruded,
After the solution heat treatment, a high temperature corrosion test and a creep rupture test were performed. High temperature corrosion test is 37% NaCl + 63% F
eCl 2 synthetic ash was applied to the surface of the plate-shaped test piece, and 0.2% H
Cl + 0.5% SO 2 + 5% O 2 + 15% CO 2 + ba
l. The sample was heated in N 2 gas at 550 ° C. for 30 hours, and the corrosion depth of the vertical cross section of the test piece was measured. The creep rupture test is a test piece with a gauge of φ6 × l 30mm, temperature 550 ℃, application 44
The creep rupture strength was evaluated by the rupture time under the condition of 1.3 N / mm 2 . The hot workability was evaluated by the presence or absence of cracks during hot extrusion.
【００１５】表１、表２に示す本発明例Ａ〜Ｃは２０Ｃ
ｒ−２５Ｎｉ−１．５Ｍｏを基本成分として、Ａｌをそ
れぞれ１％、３％および５％含有したものであり、Ｄ〜
Ｆは同一基本成分にＳｉをそれぞれ１％、２％および３
％含有したものである。また、本発明例Ｇ〜Ｉは２４Ｃ
ｒ−３５Ｎｉ−１．５Ｍｏを基本成分とし、Ａｌをそれ
ぞれ１％、３％および５％含有したものであり、Ｊは同
一基本成分にＳｉを２％含有したものである。The invention examples A to C shown in Tables 1 and 2 are 20C.
r-25Ni-1.5Mo as a basic component, containing 1%, 3% and 5% of Al, respectively.
F contains 1%, 2% and 3% of Si in the same basic component, respectively.
% Contained. The invention examples G to I are 24C.
r-35Ni-1.5Mo is a basic component, Al is contained by 1%, 3% and 5% respectively, and J is the same basic component by containing Si by 2%.
【００１６】次に、Ｋ、Ｌは２０Ｃｒ−２５Ｎｉ−１．
５Ｍｏを基本成分として、Ａｌ、ＳｉをＫはそれぞれ３
％、１％、Ｌはそれぞれ１％、２％複合で含有したもの
であり、Ｍ、Ｎは２４Ｃｒ−３５Ｎｉ−１．５Ｍｏを基
本成分とし、Ａｌ、ＳｉをＭはそれぞれ３％、１％、Ｎ
はそれぞれ１％、２％複合で含有したものである。本発
明例ＯはＢの２0Ｃｒ−２５Ｎｉ−１．５Ｍｏ−３Ａｌ
に対し、Ｎｉが１８％と低く、ＰはＧの２４Ｃｒ−３５
Ｎｉ−１．５Ｍｏ−１Ａｌに対し、Ｎｉが４６％と高
い。Ｑ〜ＳはＢの２０Ｃｒ−２５Ｎｉ−１．５Ｍｏ−３
Ａｌに対し、それぞれＭｏが２．７％、Ｔｉが０．２５
％およびＮｂが０．５１％と高い。Next, K and L are 20Cr-25Ni-1.
With 5Mo as the basic component, Al and Si are each 3 K
%, 1%, and L are 1% and 2% respectively, and M and N are 24Cr-35Ni-1.5Mo as a basic component, and Al and Si are 3% and 1%, respectively. N
Are those containing 1% and 2% respectively. Inventive Example O is B of 20Cr-25Ni-1.5Mo-3Al.
On the other hand, Ni is as low as 18%, and P is 24Cr-35 of G.
Ni is as high as 46% with respect to Ni-1.5Mo-1Al. Q to S are 20Cr-25Ni-1.5Mo-3 of B
Mo is 2.7% and Ti is 0.25 with respect to Al.
% And Nb are as high as 0.51%.
【００１７】本発明例Ａ〜Ｓはいずれも高温腐食深さ５
０μｍ以下の良好な高温腐食特性、２００ｈ以上の良好
なクリープ破断強度および熱間押出時に割れの見られな
い良好な熱間加工性を有している。一方、表３、表４に
示す比較例ＨＡ〜ＨＧはＮｉをそれぞれ８．９％、１
３．０％、１７．５％、２５．１％、３４．８％、４
６．３％および５４．０％を含有するオーステナイト系
ステンレス鋼であり、いずれの鋼もＡｌおよびＳｉが本
発明の成分範囲下限である０．５％および０．７％より
低い。なお、ＨＡはＳＵＳ３０４相当であり、Ｎｉが本
発明の成分範囲（１７〜５０％）より低い。In each of Examples A to S of the present invention, the high temperature corrosion depth was 5
It has a good high temperature corrosion property of 0 μm or less, a good creep rupture strength of 200 h or more, and a good hot workability in which no crack is observed during hot extrusion. On the other hand, in Comparative Examples HA to HG shown in Tables 3 and 4, Ni was 8.9% and 1 respectively.
3.0%, 17.5%, 25.1%, 34.8%, 4
It is an austenitic stainless steel containing 6.3% and 54.0%, and both Al and Si are lower than 0.5% and 0.7% which are the lower limits of the composition range of the present invention. HA is equivalent to SUS304, and Ni is lower than the component range (17 to 50%) of the present invention.
【００１８】ＨＨはＡｌを３％含有するが、Ｎｉが１３
％で本発明の成分範囲より低い。次に、ＨＩ、ＨＪは２
４Ｃｒ−３５Ｎｉ−１．５Ｍｏを基本成分として、ＨＩ
はＡｌが６．７％、ＨＪはＳｉが３．６％で、いずれも
本発明の成分範囲を超えて含有した鋼である。さらに、
ＨＫは２４Ｃｒ−３５Ｎｉ−１．５Ｍｏを基本成分とし
て、ＡｌおよびＳｉをそれぞれ６．８％および３．５％
含有し、両成分共に本発明の成分範囲を超えた鋼であ
る。HH contains 3% Al, but Ni is 13%.
%, Lower than the component range of the present invention. Next, HI and HJ are 2
With 4Cr-35Ni-1.5Mo as the basic component, HI
Is 6.7% Al, and HJ is 3.6% Si, both of which are steels containing more than the composition range of the present invention. further,
HK has 24Cr-35Ni-1.5Mo as a basic component and Al and Si at 6.8% and 3.5%, respectively.
It is a steel that contains both components and exceeds both the components of the present invention.
【００１９】また、ＨＬ〜ＨＯは２０Ｃｒ−２５Ｎｉ−
１．５Ｍｏを基本成分として、Ａｌを３％含有するが、
ＨＬはＭｏが０．１０％で本発明の成分範囲より低く、
ＨＭはＴｉとＮｂが共に無添加、ＨＮはＴｉが無添加、
ＨＯはＮｂが無添加でいずれも本発明の成分範囲外の鋼
である。これらの比較例は、本発明例と対比して、高温
腐食特性、クリープ破断強度あるいは熱間加工性の少な
くともいずれか一特性に問題点を有している。HL to HO are 20Cr-25Ni-
It contains 1.5Mo as a basic component and 3% Al,
HL has a Mo content of 0.10%, which is lower than the component range of the present invention.
Both Ti and Nb are not added to HM, Ti is not added to HN,
HO is a steel which does not contain Nb and is outside the composition range of the present invention. Compared with the examples of the present invention, these comparative examples have a problem in at least one of high temperature corrosion properties, creep rupture strength and hot workability.
【００２０】すなわち、ＡｌおよびＳｉが共に本発明の
成分範囲下限より低いＨＡ〜ＨＧと、Ａｌを３％含有す
るがＮｉが本発明の成分範囲下限より低いＨＨは高温腐
食深さが５０μｍを超えて、高温腐食特性が本発明鋼よ
り劣る。Ａｌが６．７％のＨＩおよびＳｉが３．６％の
ＨＪはＡｌ、Ｓｉがそれぞれ本発明の成分範囲上限より
高く、クリープ破断強度が本発明例より低い。また、Ａ
ｌおよびＳｉを共に本発明の成分範囲を超えて含有する
ＨＫは熱間押出時に大きな割れが発生し、高温腐食特性
およびクリープ破断強度評価用試験片が採取できなかっ
た。That is, HA to HG in which Al and Si are both lower than the lower limit of the composition range of the present invention, and HH which contains 3% of Al but Ni is lower than the lower limit of the composition range of the present invention has a high temperature corrosion depth of more than 50 μm. Therefore, the high temperature corrosion property is inferior to that of the steel of the present invention. HI with Al of 6.7% and HJ with Si of 3.6% each have Al and Si higher than the upper limits of the component ranges of the present invention and a lower creep rupture strength than the inventive examples. Also, A
For HK containing both 1 and Si in excess of the component ranges of the present invention, large cracks were generated during hot extrusion, and test pieces for evaluating high temperature corrosion characteristics and creep rupture strength could not be collected.
【００２１】次に、Ａｌを３％含有するが、Ｍｏ、Ｔｉ
およびＮｂのうち１種以上が本発明の成分範囲下限より
低いＨＬ〜ＨＯはクリープ破断強度が本発明例より低
い。なお、熱間加工性評価では、熱間押出時に大きな割
れが発生した上述のＨＫの他に、Ｎｉを本発明の成分範
囲を超えて５４％含有するＨＧ、ＡｌあるいはＳｉが本
発明の成分範囲上限より高いＨＩ、ＨＪで熱間押出時に
ヘゲ状疵が発生した。Next, although containing 3% Al, Mo, Ti
And HL to HO in which at least one of Nb is lower than the lower limit of the component range of the present invention, the creep rupture strength is lower than that of the present invention. In addition, in the hot workability evaluation, in addition to the above-mentioned HK in which large cracks occurred during hot extrusion, HG, Al or Si containing 54% of Ni in excess of the composition range of the present invention is the composition range of the present invention. With HI and HJ higher than the upper limit, bald defects occurred during hot extrusion.
【００２２】[0022]
【表1】 【table 1】
【００２３】[0023]
【表2】 [Table 2]
【００２４】[0024]
【表３】 [Table 3]
【００２５】[0025]
【表４】 [Table 4]
【００２６】[0026]
【発明の効果】本発明によれば、廃棄プラスチック類お
よび自動車シュレッダーダスト等の廃棄物燃焼ボイラの
過熱器管等に用いられる、燃焼環境中の溶融塩化物およ
び塩化水素（ＨＣｌ）ガス等に対して優れた高温腐食特
性を有し、かつクリープ破断強度の良好なオーステナイ
ト系ステンレス鋼を供給することが可能になり、エネル
ギーおよび環境分野に極めて有用な効果がもたらされ
る。EFFECTS OF THE INVENTION According to the present invention, for molten chloride and hydrogen chloride (HCl) gas in a combustion environment, which is used in waste plastic boilers and superheater tubes of waste combustion boilers such as automobile shredder dust, etc. It becomes possible to supply an austenitic stainless steel having excellent high temperature corrosion characteristics and excellent creep rupture strength, which brings a very useful effect in the fields of energy and environment.
【図１】高温腐食深さに及ぼすＮｉ含有量の影響を示す
図である。FIG. 1 is a diagram showing the effect of Ni content on high temperature corrosion depth.
【図２】高温腐食深さに及ぼすＡｌおよびＳｉ含有量の
影響を示す図である。FIG. 2 is a diagram showing the influence of Al and Si contents on high temperature corrosion depth.
Claims (1)
する高温腐食特性に優れたオーステナイト系ステンレス
鋼。Claims: 1. C .: 0.02 to 0.15%, Mn: 0.3 to 2.0%, Cr: 18 to 25%, Ni: 17 to 50 in% by weight. %, Mo; 0.5 to 3.0%, Ti; 0.03 to 0.3%, Nb; 0.05 to 0.6%, B; 0.003 to 0.01%, P; 04% or less, S; 0.005% or less, N; 0.02-0.3%, Ca; 0.0005-0.05%, and Al; 0.5-6.0%, Si An austenitic stainless steel excellent in high-temperature corrosion characteristics, characterized by containing at least one of 0.7 to 3.0% and the balance being Fe and unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3165946A JPH0826439B2 (en) | 1991-07-05 | 1991-07-05 | Austenitic stainless steel with excellent high temperature corrosion properties |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3165946A JPH0826439B2 (en) | 1991-07-05 | 1991-07-05 | Austenitic stainless steel with excellent high temperature corrosion properties |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH059659A true JPH059659A (en) | 1993-01-19 |
| JPH0826439B2 JPH0826439B2 (en) | 1996-03-13 |
Family
ID=15822026
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3165946A Expired - Lifetime JPH0826439B2 (en) | 1991-07-05 | 1991-07-05 | Austenitic stainless steel with excellent high temperature corrosion properties |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0826439B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7325754B2 (en) | 2002-09-20 | 2008-02-05 | Toto Ltd. | Shower nozzle |
| JP2008545889A (en) * | 2005-06-03 | 2008-12-18 | エイティーアイ・プロパティーズ・インコーポレーテッド | Austenitic stainless steel |
| EP2016031A1 (en) * | 2006-05-02 | 2009-01-21 | Sandvik Intellectual Property AB | A component for supercritical water oxidation plants, made of an austenitic stainless steel alloy |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS52143913A (en) * | 1976-05-25 | 1977-11-30 | Nippon Steel Corp | Two phases stainless steel |
| JPS5424214A (en) * | 1977-07-27 | 1979-02-23 | Daido Steel Co Ltd | Heattresistant steel having good heat fatigue characteristic |
| JPS60230966A (en) * | 1984-04-27 | 1985-11-16 | Sumitomo Metal Ind Ltd | Steel for dry and corrosive environment containing chloride at high temperature |
-
1991
- 1991-07-05 JP JP3165946A patent/JPH0826439B2/en not_active Expired - Lifetime
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS52143913A (en) * | 1976-05-25 | 1977-11-30 | Nippon Steel Corp | Two phases stainless steel |
| JPS5424214A (en) * | 1977-07-27 | 1979-02-23 | Daido Steel Co Ltd | Heattresistant steel having good heat fatigue characteristic |
| JPS60230966A (en) * | 1984-04-27 | 1985-11-16 | Sumitomo Metal Ind Ltd | Steel for dry and corrosive environment containing chloride at high temperature |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7325754B2 (en) | 2002-09-20 | 2008-02-05 | Toto Ltd. | Shower nozzle |
| JP2008545889A (en) * | 2005-06-03 | 2008-12-18 | エイティーアイ・プロパティーズ・インコーポレーテッド | Austenitic stainless steel |
| EP2016031A1 (en) * | 2006-05-02 | 2009-01-21 | Sandvik Intellectual Property AB | A component for supercritical water oxidation plants, made of an austenitic stainless steel alloy |
| EP2016031A4 (en) * | 2006-05-02 | 2011-03-16 | Sandvik Intellectual Property | A component for supercritical water oxidation plants, made of an austenitic stainless steel alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0826439B2 (en) | 1996-03-13 |
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